High density lithium cobalt oxide for rechargeable batteries

ABSTRACT

The disclosure relates to positive electrode material used for Li-ion batteries, a precursor and process used for preparing such materials, and Li-ion battery using such material in its positive electrode. The disclosure describes a higher density LiCoO 2  positive electrode material for lithium secondary batteries, with a specific surface area (BET) below 0.2 m 2 /g, and a volumetric median particle size (d50) of more than 15 μm. This product has, improved specific capacity and rate-capability. Other embodiments of the disclosure are an aggregated Co(OH) 2 , which is used as a precursor, the electrode mix and the battery manufactured using abovementioned LiCoO 2 .

This application is a National Stage application of International Application No. PCT/EP2008/004629, filed Jun. 10, 2008, which claims the benefit of European Patent Application No. 07012781.6, filed Jun. 29, 2007, U.S. Provisional Application No. 60/929,614, filed Jul. 5, 2007, and European Patent Application No. 07023548.6, filed Dec. 5, 2007, the entire contents of each are hereby incorporated herein by reference.

The invention relates to positive electrode material used for Li-ion batteries, a precursor and process used for preparing such materials, and Li-ion battery using such material in its positive electrode.

Compared to Ni—Cd and Ni-MH rechargeable batteries, Li-ion batteries boast an enhanced energy density, mainly due to their higher 3.6 V working voltage. Since their commercialization in 1991 by SONY, Li-ion batteries have seen their volumetric energy density increase continuously. In 1995, the capacity of a typical 18650 cylindrical cell was about 1.3 Ah. In 2006, the capacity of the same type of cell is about 2.6 Ah. Such a high energy density has enabled a wide range of applications. Li-ion batteries have become the dominant secondary battery for portable application, representing a market share of about 70% in 2006.

Such significant increase of energy density of Li-ion batteries has been initially realized by optimizing cell design, accommodating more active electrode materials in a fixed volume cell. Later efforts concentrated on improving the energy density of the electrodes. Using a high density active electrode material is one way to achieve this goal. As LiCoO₂ still continues to be used as positive electrode material for the majority of commercial Li-ion batteries, a highly dense variety of this material is in demand.

The tap density of electrode materials is usually a good indicator of electrode density. However, in some cases, a high tap density does not guarantee a high electrode density. For example, as demonstrated by Ying et al. (Journal of power Sources, 2004) or in CN1206758C, the tap density of a LiCoO₂ powder with large secondary spherical particle size, but small primary size, can be as high as 2.8 g/cm³. However, because of its small primary particle size, and possibly because of voids in the secondary particles, the obtained electrode density is not correspondingly high. For this reason, density of electrode materials should preferably be measured under a pressure similar to the industrial conditions prevailing during actual electrode manufacture, instead of by tapping. In this invention, density therefore refers to press density, and not to tap density.

The theoretical density of LiCoO₂ is about 5.1 g/cm³. For actual LiCoO₂ powders, factors that impact the density are a.o. the shape of particles, the size of primary particles and the particle size distribution. In today's industry, the medium primary particle size of LiCoO₂ used for different application is in the range of 1 to 20 μm. Generally, the larger the median primary particle size (d50), the higher is the press density. In addition, as proposed in CN1848491A, electrode density can be increased further by mixing larger LiCoO₂ particles with 15 to 40 wt % of finer particles.

Besides density reasons, a large median primary particle size is also desirable for safety purposes, especially for large cells such as the 18650 model cylindrical cells that are used in laptop computer. During charge, lithium atoms in LiCoO₂ are partially removed. LiCoO₂ becomes Li_(1-x)CoO₂ with x>0. At high temperatures caused by certain abuse condition, Li_(1-x)CoO₂ tends to decompose and then to release O₂. The released O₂ easily reacts with organic solvent in the battery electrolyte, resulting in fire or explosion of the battery. Using LiCoO₂ with a large median primary particle size and low specific surface area (BET) reduces these risks, as pointed out by Jiang J. et al. (Electrochimica Acta, 2004).

Therefore, for both safety and energy density reasons, LiCoO₂ with large median primary particle size, such as 15 μm or above, is preferred, in particular for large Li-ion cells. Materials with a large mass median primary particle size (d50) have also a relatively low BET. A d50 larger than 15 μm typically leads to a BET below 0.2 m²/g.

In a usual manufacture process of LiCoO₂, powderous Co₃O₄ and Li₂CO₃ are mixed and then fired at a temperature ranging from 800° C. to 1100° C. The d50 of the Co₃O₄ needs to be relatively small, usually below 5 μm, to ensure a sufficient reactivity. The growth of the LiCoO₂ particles is controlled by the firing temperature and time, and by the amount of excess Li (added as Li₂CO₃). To make LiCoO₂ with a d50 larger than 15 μm, at least 6 at. % of excess Li per Co atom is needed, as this excess favours crystal growth. However, part of the excess Li also enters the LiCoO₂ structure. Therefore, the final product will be Li over-stoichiometric. This is why all current LiCoO₂ material with large primary particle size (or a low BET, which is equivalent) is significantly over-stoichiometric. Due to this excess Li in their structure, such materials have a lower capacity because some active Co³⁺ has been replaced by inactive Li⁺. In this respect, it should be noted that in this application, LiCoO₂ is used to designate a wide variety of lithium cobalt oxides having stoichiometries that may slightly deviate from the theoretical.

One example of this process can be found in EP 1 281 673 A1. Here a composition LiCo_((1-x))Mg_(x)O₂ is disclosed, wherein x is 0.001 to 0.15, and having an average particle diameter of 1.0 to 20 μm and a BET of 0.1 to 1.6 m²/g. However, the examples clearly show that the inventor did not succeed in manufacturing a lithium cobalt (magnesium) oxide powder having both of: a d50 of more than 15 μm, and a specific surface area (BET) of less than 0.2 m²/g. The maximum d50 achieved in this document is 8.3 μm in a comparative example.

It is finally also desirable for electrode materials to provide good rate capability. Rate capability is defined as the ratio of specific discharge capacity at a higher discharge rate (typically 2 C), to the specific discharge capacity at a lower rate (typically 0.1 C). Unfortunately, current LiCoO₂ with large primary particle size shows relatively poor rate capability, as shown in JP3394364 and by Chen Yan-bin et al. (Guangdong Youse Jinshu Xuebao, 2005). Such poor rate capability is considered to be related to the longer Li diffusion path for material with larger primary particle size when Li is removed or reinserted during charge or discharge.

In summary, LiCoO₂ with a large primary particle size is preferred for Li-ion battery for improved safety and energy density. However, current large particle size powders show sub-optimal capacity and rate capability because of the significant Li-excess in their structure.

A first principal objective of this invention is therefore to provide a relatively coarse-grained electrochemically active LiCoO₂ powder, without significant Li-excess.

The first active product embodiment of the invention concerns a lithium cobalt oxide powder for use as an active positive electrode material in lithium-ion batteries, having a d50 of more than 15 μm, a BET of less than 0.2 m²/g, and a Li to Co atomic ratio between 0.980 and 1.010, preferably of less than 1.000, more preferably of less than 0.999. The mentioned particle size is evidently a primary particle size, and the particles are neither agglomerated or coagulated, nor aggregated.

This Li to Co ratio range is chosen so that such composition gives a discharge capacity of more than 144 mAh/g at 2 C, and rate capability (Q2 C/Q0.1 C) of more than 91%. For product with an Li to Co ratio lower than 0.980, electrochemically inactive and thus undesired Co₃O₄ has been identified with X-ray diffraction.

It should be mentioned that in US 2002/119371 A1 an electrochemically active material is used, having the formula of a ternary (Li-Me1-O) or quaternary (Li-Me1-Me2-O) lithium transition metal oxides, wherein Me1 and Me2 are selected from the group consisting of Ti, V, Cr, Fe, Mn, Ni, Co. It can further comprise up to about 15 atom percent of Mg, Al, N or F to stabilize the structure, and have a BET of 0.1-2 m²/g and a particle size of from about 1 to about 50 μm. However, the ratio Li/Co is said to be in the wide range of 0.98 to about 1.05, without giving a more specific example.

Also, in EP 1 052 716 A2 a Li-transition metal composite oxide Li_(A)M_((1-x))Me_(x)O₂ is disclosed, with M being Co, Ni, Mn, V, Ge and the like, and preferably LiCoO₂, where A is 0.05-1.5, preferably 0.1-1.1, and x can be zero. This composite oxide preferably has an average particle size of 10-25 μm, and also preferably has a BET of 0.1-0.3 m²/g. In the examples (Table 1) however, the combination of average particle size above 15 μm and BET under 0.2 m²/g is not disclosed together with a Li/Co atomic ratio between 0.980 and 1.010.

The second active product embodiment of the invention concerns a lithium cobalt oxide powder for use as an active positive electrode material in lithium-ion batteries, having a d50 of more than 15 μm, a BET of less than 0.2 m²/g, and with an OH⁻ content between 0.010 and 0.015 wt % more preferably between 0.0125 and 0.015.

This OH⁻ range was found to correspond to the nearly stoichiometric products delivering the optimal electrochemical performances. By OH⁻ content is meant the OH⁻ as determined by acid-base titration of an aqueous dispersion of the lithium cobalt oxide powder. Titration is performed using a 0.1 M HCl solution. As some carbonates could be present, the relevant amount of acid is calculated as the amount of acid to reach pH 7, minus the amount of acid to reach pH 4 from pH 7.

It should be mentioned here that in US 2006/263690 A1 a positive electrode material

Li_(p)Co_(x)M_(y)O_(z)F_(a) is claimed, where 0.9≦p≦1.1, y and a may be zero (and x=1), 1.9≦z≦2.1. D50 is from 5 to 15 μm (although also up to 20 μm is mentioned singularly), and BET from 0.3 to 0.7 m²/g. This lithium composite oxide has a remaining alkali amount of at most 0.02, and preferably at most 0.01 wt %. All of the examples show a combination of a BET value over 0.2 m²/g, and a D50 under 15 μm.

In WO99/49528 (equivalent to EP 1 069 633 A1) on the other hand, a LiCoO2 is disclosed which comprises a mixture of primary particles of small crystals having a Feret's diameter in a projection drawing by SEM observation in a range from 0.4 to 10 μm and an average diameter of 5 μm or less, and secondary particles formed by ‘gathering’ of the primary particles and having a diameter of 4 to 30 μm, wherein the mole ratio of Co to Li is 0.97 to 1.03, and at least a part of small crystals constituting the secondary particles are joint by the junction through sintering, and the secondary particles are in the shape of a circle or an ellipse. This material is preferably obtained by mixing a lithium salt and a cobalt source where cobalt oxyhydroxide (CoOOH) is used as a raw material and comprises secondary particles falling in the range of 4 to 30 μm and formed by gathering of a number of primary particles of 0.2 to 0.8 μm and subsequently, by carrying out a heat treating on this mixture.

The characteristics of both the first and second embodiments of the invention mentioned before can advantageously be combined.

The above mentioned dependency of capacity and rate capability on the Li to Co ratio is also applicable to doped products, in particular for Mg-doped LiCoO₂. A third active product embodiment is therefore a lithium cobalt oxide powder for use as an active positive electrode material in lithium-ion batteries according to embodiments 1 and 2, further comprising Mg as doping elements with a Mg to Co atomic ratio between 0.001 to 0.05. However, in this case, it is the atomic ratio of Li to the sum of Co and Mg (instead of to Co alone) that should be between 0.980 and 1.010, and be preferably less than 1.000, and more preferably less than 0.999.

As described above, mixing relatively coarse lithium cobalt oxide powder with finer powder can further increase the electrode density. Therefore, the fourth active product embodiment of this invention is defined a powder mixture for use as an active positive electrode material in lithium-ion batteries, comprising at least 50% by weight of a first powder according to any one of embodiments one to three, and comprising a second powdered active component consisting of lithium transition-metal oxide. The said second powder should preferably be finer than said first powder, and, in particular result in a powder mixture showing a bimodal particle size distribution.

Such a bimodal powder mixture should preferably comprise an electrochemically active second powder, consisting of lithium cobalt oxide, the mixture having a BET of less than 0.5 m²/g.

A second principal objective of this invention is to provide an economical precursor that can be used to manufacture the invented products effectively and economically.

Usually, LiCoO₂ is made by solid state reaction of Co₃O₄ as a Co source with Li₂CO₃ as a Li source.

As explained above, the customary use of Co₃O₄ as a precursor for LiCoO₂ has been found to imply the addition of excess Li when large particle sizes are sought, this excess resulting in undesired side effects, such as reduced capacity and rate capability. Moreover, and from the point of view of process robustness, it appears that the mass median primary particle size (d50) of the LiCoO₂ product is very sensitive to variations of the firing temperature and of the Li-excess. Indeed, a 10° C. variation in firing temperature causes a d50 change of 2 to 3 μm, and a 1% variation in Li causes a d50 change of 2 to 4 μm. Therefore, using Co₃O₄, a very strict control of the Li to Co blending ratio and of the firing temperature is required in order to obtain a consistent result. Such a control is difficult to ensure, in particular when production is envisaged at an industrial scale.

This problem does not occur when using a specially prepared aggregated Co(OH)₂ as a precursor. Moreover, Co₃O₄ is relatively expensive compared to other alternatives such as Co(OH)₂. To reduce costs, Co(OH)₂ has therefore already been proposed to replace Co₃O₄ as a cheaper Co source, as for example in JP2002321921. However, two firing steps are needed according to the described process. Due to the high costs of such a double firing process, the total savings remain limited.

According to the inventors' results, the shape of the aggregated Co(OH)₂ precursor particles can be preserved after firing with a Li precursor. The secondary particle size of the end product is only slightly smaller than that of aggregated Co(OH)₂ precursor. The primary particle size of LiCoO₂ still depends on the firing conditions, such as Li to Co ratio, firing temperature and firing time.

With the invented aggregated precursor, using a suitable blending ratio of Li to Co, and a single firing step, the primary particles in the end product grow larger, while there is little change in secondary particle size. Under certain conditions, such as with a blending ratio of Li to Co between 1.04 and 1.06, and a firing temperature in the range of 960 to 1020° C., the primary particles forming the secondary structure can indeed grow together. In this way, and by using aggregated Co(OH)₂, the products mentioned in the aforementioned embodiments can be prepared cost effectively.

A precursor product according to this invention is thus defined as either one or more of an non-sintered agglomerated powderous cobalt oxide, hydroxide and oxy-hydroxide, having a secondary particle size with a d50 of more than 15 μm. Preferably the primary particles have a primary particle size with a d50 of less than 5 μm. The secondary particles preferably have a spherical shape. The cobalt oxide can either be Co₃O₄, Co₂O₃, or a partially oxidized and dried Co(OH)₂. It is important that the secondary particles of the precursor do not contain any sintered primary particles, since the desired result can only be obtained using a single firing step.

A third principal objective of this invention concerns a process for manufacturing the invented active products, starting from the invented precursor products.

To this end, a process is defined whereby the Co precursor is mixed with Li source, according to a Li to Co ratio in the range between 1.04 and 1.06, and firing the mixture with a single firing at temperature between 960° C. and 1020° C. This single-firing process comprises the steps of:

-   -   providing for a precursor compound as described above,     -   mixing said precursor compound with a Li source according to a         Li to Co ratio R between 1.04 and 1.06, and     -   firing said mixture with a single firing at a temperature T         between 960° C. and 1020° C., whereby the quotient Q of the         firing temperature T and the Li to Co ratio R corresponds to         920≦Q≦965. When 1.04≦R≦1.05, then preferably 920≦Q≦960, and more         preferably 925≦Q≦945. When 1.05<R≦1.06, then preferably         925≦Q≦965, and more preferably 945≦Q≦960.

Another objective of the invention is to provide Li-ion batteries with increased energy density and rate capability. With the product mentioned in the first embodiment, the capacity and rate capability of a cell with certain volume can be increased. Therefore the energy density and rate capability can be improved.

Finally, this invention also concerns Li-ion batteries that use the product mentioned in the abovementioned active product embodiments, as positive electrode materials.

The following figures illustrate the invention.

FIG. 1: Discharge capacity and rate capability vs. the Li to Co ratio for LiCoO₂ with a BET of 0.15 to 0.18 m²/g and a d50 of 15.7 to 18.2 μm.

FIG. 2: Discharge capacity and rate capability vs. OH⁻ content for LiCoO₂ with a BET of 0.15 to 0.18 m²/g and a d50 of 15.7 to 18.2 μm.

FIG. 3: XRD diffraction pattern of Example 1 (a) and Comparative Example 2 (b).

FIG. 4: SEM image of the aggregated precursor used in Examples 1, 2, and 3.

FIG. 5: SEM image of final product according to Example 1.

FIG. 6: SEM image of final product according to Comparative Example 3.

Products with similar medium particle size (in the range of 15.7 μm to 18.2 μm) and similar BET (in the range of 0.15 m²/g to 0.18 m²/g) but with various Li to Co ratios (in the range of 0.95 to 1.02) were prepared. Particle size and specific surface area of all products studied were kept nearly constant. The Li diffusion path lengths for the different products are therefore comparable. The variation in discharge capacity (Q) at low rate (0.1 C) and at high rate (2 C) amongst the products therefore can be attributed to variation of the Li to Co ratio. According to electrochemical results, as shown in FIG. 1, products with a Li to Co ratio in the range of 0.980 to 1.010 offer optimal characteristics: a high capacity with only a limited decrease at high rate, corresponding to a rate capability (ratio of Q@0.1 C to Q@2 C) of more than 91%. With lower Li to Co ratios, products have less capacity, probably due to the appearance of inactive Co₃O₄ impurities. For example, a significant X-ray diffraction peak of Co₃O₄ was found in the diffraction pattern of a product with a ratio of 0.970. On the other hand, products with too high Li to Co ratios lose some of their charge-discharge capacity, probably because of the substitution of active Co³⁺ by inactive Li⁺.

FIG. 2 shows a similar correlation as a function of the OH⁻ content for the same samples used in FIG. 1. The optimal OH⁻ range is 0.010 to 0.015 wt %. As OH⁻ content increases, the rate capability initially increases. However, as it increases beyond 0.015 wt %, the rate capability sharply degrades.

EXAMPLES

The present invention is described in more detail by examples and comparative examples below. However, the examples are only illustrative, and, therefore, not intended to limit the scope of the present invention.

To prepare Co(OH)₂ or Mg-doped Co(OH)₂, a suitable Co²⁺ salt, preferably CoSO₄.6H₂O, is dissolved in water. The so obtained solution typically contains about 55 g/L of Co. Co(OH)₂ is then precipitated by adding an aqueous base, preferably a solution of 25% NaOH, and a 260 g/L NH₃ to the Co solution into a stirred and heated, preferably to 62° C., overflow reactor tank. The reactor tank is typically filled with a seed slurry of Co(OH)₂ containing NaOH, Na₂SO₄, ammonia, and water. As the reaction proceeds, the resulting overflow slurry is collected, and a pink solid is separated from the supernatant by filtration. After washing with water, the solid is dried in a convection oven to a constant mass. The resulting powder is a highly pure, spheroidal, flowable, oxidation resistant Co(OH)₂ that is easily screened and processed.

Mg-doped Co(OH)₂ is produced under similar conditions as the above pure Co(OH)₂. The only difference is that instead of using a feed solution of pure CoSO₄, the feed solution is supplemented with a suitable Mg²⁺ salt, preferably MgSO₄.

During the precipitation reaction, pH (temperature uncompensated) is maintained between 10.4 and 11.3, preferably between 10.8 and 11.0. In general, a higher pH will result in the precipitation of smaller secondary particles, while a lower pH will result in the precipitation of larger secondary particles. The resulting spherical Co(OH)₂ has d50 particle size volume distribution values between 5 and 50 μm and spans (defined as (d90-d10)/d50) ranging from 0.5 to 2.0. More precisely, the steady state production of Co(OH)₂ will result in D50 particle sizes ranging from 14 to 21 μm with spans ranging from 0.9 to 1.2. Alternatively, a less spherical agglomerated Co(OH)₂ material can be produced by increasing the pH. This material retains water more easily and has steady state d50 particle sizes ranging from 4-14 μm with spans typically greater than 1.0.

Particle size distribution of LiCoO₂ is measured using a Malvern Mastersizer 2000. The median volumetric particle size is assumed to be equivalent to the median mass particle size represented by d50. The specific surface area of LiCoO₂ is measured with the Brunauer-Emmett-Teller (BET) method using a Micromeritics Tristar. To measure the press density of LiCoO₂, a mixture is made with 95 wt % active material, 2.5 wt % carbon black, and 2.5 wt % polyvinylidene fluoride (PVDF) in N-methylpyrrolidone (NMP). After drying, 1.2 g powder is put in a SPEX 3613 13 mm die set and pressed under 3.7 metric ton per cm². Press density is calculated by dividing the mass by the volume of the pressed pellet. The OH⁻ content of fired LiCoO₂ is measured by pH titration in water with a 0.1 M HCl solution.

Electrochemical performance is tested in coin type cells, with a Li foil as counter electrode in a lithium tetrafluoroborate (LiBF₄) type electrolyte at 24° C. Cells are charged to 4.3 V and discharged to 3.0 V. A specific capacity of 160 mAh/g is assumed for the determination of the discharge rates. For example, for discharge at 2 C, a specific current of 320 mA/g is used.

Example 1

A mixture is made with aggregated Co(OH)₂ with a d50 of 19.3 μm and Li₂CO₃ with a Li to Co (atomic) blending ratio of 1.05. The mixed powder is fired in air at 980° C. for 12 hours. After cooling, the obtained material is milled and screened with a 270 mesh screen.

Example 2

Same as example 1, except that the firing temperature is 970° C.

Example 3

A mixture is made with aggregated Co(OH)₂ with a d50 of 19.3 μm and Li₂CO₃ with a Li to Co blending ratio of 1.04. The mixed powder is fired in air at 990° C. for 10 hours. After cooling, the obtained material is milled and screened with a 270 mesh screen.

Example 4

A mixture is made with aggregated (Co_(0.99)Mg_(0.01))(OH)₂ with a d50 of 18.7 μm, which is dried at 175° C. for 5 hours, and Li₂CO₃ with a Li to (Co_(0.99)Mg_(0.01)) blending ratio of 1.05. The mixed powder is fired in air at 980° C. for 12 hours. After cooling, the obtained material is milled and screened with a 270 mesh screen.

Example 5

Product from Example 3 is mixed with commercially available Cellcore® D5 (Umicore, Belgium) in a 80 to 20 weight ratio. Cellcore® D5 has a d50 of 6.5 μm, which is smaller than the product from Example 3 (17.4 μm). The press density of the mixed powder is 3.83 g/cm³, which is higher than that of Example 3 (3.79 g/cm³).

Comparative Example 1

A mixture is made with Co₃O₄ with a d50 of 3 μm and Li₂CO₃ with a Li to Co blending ratio of 1.065. The mixed powder is fired in air at 960° C. for 12 hours. After cooling, the obtained material is milled and screened with a 270 mesh screen.

Comparative Example 2

A mixture is made with aggregated Co(OH)₂ with a d50 of 19.3 μm and Li₂CO₃ with a Li to Co blending ratio of 1.035. The mixed powder is fired in air at 1020° C. for 10 hours. After cooling, the obtained material is milled and screened with a 270 mesh screen.

Comparative Example 3

A mixture is made with aggregated Co(OH)₂ with a d50 of 19.3 μm and Li₂CO₃ with a Li to Co blending ratio of only 1.005. The mixed powder is fired in air at 920° C. for 12 hours. After cooling, the obtained material is milled and screened with a 270 mesh screen.

Comparative Example 4

A mixture is made with aggregated Co(OH)₂ with a d50 of only 9 μm and Li₂CO₃ with a Li to Co blending ratio of 1.06. The mixed powder is fired in air at 960° C. for 12 hours. After cooling, the obtained material is milled and screened with a 270 mesh screen.

Comparative Example 5

A mixture is made with Mg-doped Co₃O₄ (Co to Mg ratio of 99:1) with a d50 of 3 μm and Li₂CO₃ with a Li to Co blending ratio of 1.057. The mixed powder was fired in air at 960° C. for 15 hours. After cooling, the obtained material is milled and screened with a 270 mesh screen.

Comparative Example 6

A mixture is made with aggregated Co(OH)₂ with a d50 of 19.3 μm and Li₂CO₃ with a Li to Co blending ratio of 1.06. The mixed powder is fired in air at 960° C. for 12 hours. After cooling, the obtained material is milled and screened with a 270 mesh screen.

Comparative Example 7

A mixture is made with aggregated Co(OH)₂ with a d50 of 19.1 μm and Li₂CO₃ with a Li to Co blending ratio of 1.07. The mixed powder is fired in air at 950° C. for 10 hours. After cooling, the obtained material is milled and screened with a 270 mesh screen.

Physical properties and selected electrochemical results for examples and comparative examples are listed in Table 1. Even though different Li to Co ratios and temperatures are used for the Examples 1 to 3, the d50 of the particles are about the same, in the range of 17.0 to 17.4 μm. This large particle size is reflected by the low BET, which is 0.17 m²/g or below. With such a large particle size, all three examples give high press density, around 3.77 g/cm³. Regarding chemical composition, they have a Li to Co ratio of almost one. Their OH⁻ contents are in the range of 0.012 to 0.014 wt %. They have excellent discharge capacity at 2 C rate, as well as excellent rate capability.

In Comparative Example 1, Co₃O₄ is used as a precursor. The obtained LiCoO₂ has a smaller d50 than in Example 2, where Co(OH)₂ was used, even though a higher Li to Co ratio was chosen in the blend. This results in a high Li-excess in the final product. This excess penalizes the rate capability, which is poor compared to Example 2, even though the particle size is slightly smaller. Probably due to its wider particle size distribution, the product has a slightly higher press density.

The powder according to Comparative Example 2 is made at a relatively high temperature, but at a low blending ratio. The obtained powder therefore has a significant Li deficit. Its OH⁻ content is only 0.008 wt %. In this case, there is Co₃O₄ present as an impurity in the product. This is clearly shown in FIG. 3, where the product according to Example 1 is shown for reference.

The powder of Comparative Example 3 is prepared starting from the same Co(OH)₂ precursor as in Examples 1 to 3, but with a lower Li to Co ratio and a lower firing temperature. The product still has d50 of 17 μm, which is just slightly smaller than the 19.3 of the Co(OH)₂. However, this product has a low press density of only 3.52 g/cm³, because of its small primary particles and ensuing high BET of 0.45 m²/g. This example demonstrates that a large primary particle size is needed to obtain a high density LiCoO₂.

The powder of Comparative Example 4 is prepared starting from Co(OH)₂ precursor with badly formed secondary particles. Even it is blended and fired in the same conditions as Example 2, it has a d50 of only 9.8 μm and a low press density of 3.63 g/cm³. To make high density material with such a precursor having a small secondary particle size, a high Li to Co blending ratio is needed. This is not recommended because the so obtained LiCoO₂ will end up with a too high Li excess. Therefore, to make LiCoO₂ with a large primary particle size, Co(OH)₂ with large secondary particle size is needed.

TABLE 1 Precursor Blend Product d50 Li to Co Firing Li to Co OH⁻ d50 BET Density Q2C Rate Type (μm) (at./at.) (° C.) (at./at.) (wt %) (μm) (m²/g) (g/cm³) (mAh/g) (%) Ex. 1 Co(OH)₂ 19.3 1.05 980 0.998 0.013 17.4 0.15 3.76 147.4 91.8 Ex. 2 Co(OH)₂ 19.3 1.05 970 0.999 0.014 17.0 0.17 3.75 147.8 92.2 Ex. 3 Co(OH)₂ 19.3 1.04 990 0.984 0.012 17.4 0.14 3.79 146.2 91.2 Comp Co₃O₄ 3 1.065 960 1.016 0.018 13.9 0.19 3.79 141.0 88.9 Ex. 1 Comp Co(OH)₂ 19.3 1.035 1020 0.963 0.008 17.8 0.16 3.76 141.7 89.9 Ex. 2 Comp Co(OH)₂ 19.3 1.005 920 17 0.45 3.52 Ex. 3 Comp Co(OH)₂ 9 1.06 960 9.8 3.63 Ex. 4 Comp Co(OH)₂ 19.3 1.06 960 1.019 0.021 18.2 0.16 3.78 142.8 89.9 Ex. 6 Comp Co(OH)₂ 19.1 1.07 950 1.025 0.041 23.2 0.13 3.78 140.6 89.2 Ex. 7

Table 2 lists results related to Mg-doped products. The product according to Example 4 has about the same density as the product according to Comparative Example 5. With a Li to Co-plus-Mg ratio close to 1.0, Example 4 boasts a higher capacity and a better rate capability than Comparative Example 5.

TABLE 2 Product Precursor Blend Li to d50 Li to Co Firing (Co + Mg) d50 BET Density Q2C Rate Type (μm) (at./at.) (° C.) (at./at.) (μm) (m²/g) (g/cm³) (mAh/g) (%) Ex. 4 Co(OH)₂ 18.7 1.05 980 0.996 20.1 0.18 3.79 137.2 87.5 Co/Mg = 99 Comp Co₃O₄ 3 1.057 980 1.017 17.3 0.16 3.78 134.8 86.8 Ex. 5 Co/Mg = 99

Example 5 is the result of mixing powder from Example 4 with 20% of LiCoO2 with a smaller d50. Press density increases from 3.79 g/cm³ to 3.83 g/cm³.

In Table 3 the process characteristics are investigated. In fact, to obtain the stoichiometric high density LiCoO₂ according to the invention, the correct combination of blending ratio R (=Li/Co) and firing temperature T should be respected, as listed in the following table.

TABLE 3 R vs T diagram R T 1.04 1.045 1.05 1.055 1.06 960 ✓ Over Over Over 970 ✓ ✓ ✓ Over Over 980 ✓ ✓ ✓ ✓ Over 990 ✓ ✓ ✓ ✓ ✓ 1000 Under ✓ ✓ ✓ ✓ 1010 Under Under ✓ ✓ 1020 Under Under Under ✓

In the table, “Over” means that an excess of Li is used for a firing temperature that is too low. On the contrary, “Under” stands for firing at a temperature which is too high for the given Li/Co ratio. For “√” the correct conditions are used. 

1. A lithium cobalt oxide powder for use as an active positive electrode material in lithium-ion batteries, having a d50 of more than 15 μm, a specific surface area (BET) of less than 0.2 m²/g, a Li to Co atomic ratio between 0.980 and 1.010, and an OH⁻ content between 0.010 and 0.015 wt %.
 2. The lithium cobalt oxide powder of claim 1, further comprising Mg as a doping element, having a Mg to Co atomic ratio between 0.001 and 0.05, and having a Li to the sum of Co and Mg atomic ratio between 0.980 and 1.010.
 3. A powder mixture for use as an active positive electrode material in lithium-ion batteries, comprising at least 50% by weight of a first powder, wherein the first powder is the lithium cobalt oxide powder of claim 1, and a second powderous active component consisting of a lithium transition-metal oxide.
 4. The powder mixture of claim 3, wherein the median particle size of the second powderous active component is smaller than that of the first powder, and wherein the particle size distribution of the powder mixture is multi modal.
 5. The powder mixture of claim 4, wherein the second powderous active component consists of lithium cobalt oxide, the mixture having a BET of less than 0.5 m²/g.
 6. An electrode mix comprising the powder of claim 1 as an active material.
 7. A lithium-ion battery comprising the electrode mix of claim
 6. 8. A single firing process for manufacturing the lithium cobalt oxide powder of claim 1, comprising: providing a precursor compound consisting of either one or more powderous non-sintered agglomerated cobalt oxide, hydroxide and oxyhydroxide having a secondary particle size d50 or more than 15 μm, mixing said precursor compound with a Li source according to a Li to Co ratio R between 1.04 and 1.06 to obtain a mixture, and firing said mixture with a single firing at a temperature T between 960° C. and 1020° C., whereby the quotient Q of the firing temperature T and the Li to Co ratio R corresponds to 920≦Q≦965.
 9. The single firing process of claim 8, wherein 1.04≦R≦1.05 and 920≦Q≦960.
 10. The single firing process of claim 8, wherein 1.05<R≦1.06 and 925≦Q≦965. 